The Relationship between Residual Stresses and Transverse Weld Cracks in Thick Steel Plate

Transcription

1 WELDING RESEARCH The Relationship between Residual Stresses and Transverse Weld Cracks in Thick Steel Plate The relationship between longitudinal residual stresses (Gx direction) and transverse weld cracks was studied for EH32 TMCP 50-mm-thick plate welded with the SAW and FCA W processes BY H. W. LEE AND S. W. KANG ABSTRACT. The transverse crack, a type of cold crack, occurs perpendicular to the axis of the weld interface. From experience, longitudinal residual stresses (Ox direction) are important factors in transverse crack occurrence. Specimens were fabricated and welded under actual construction conditions, then longitudinal residual stresses were measured for different welding conditions using the submerged arc welding (SAW) and flux cored arc welding (FCAW) processes. Transverse weld cracks were detected in specimens welded with preheating and an interpass temperature below 30 C using the FCAW process. Cracks were detected at mm from the weld face. But in specimens welded with preheating at 70 C, with an interpass temperature below 30 C, and using the SAW process, cracks were detected mm from the weld face (Refs. 1, 3). The residual stress values for specimens welded at an interpass temperature below 30 C were higher than specimens welded with interpass temperatures of C. Also, the residual stress values measured at the weld surface, in the as-welded condition, were higher than longitudinal residual stresses measured from a small test piece due to residual stress relief from the cutting and machining processes. Transverse weld cracks were detected in the area of maximum residual stresses for both the SAW and FCAW processes. Introduction Residual stresses are developed in the vicinity of a weld joint during arc welding. H. W LEE is with the Welding Research Team of Samsung Heavy Industries, Koje City, Korea. S. W KANG is with the Research Institute of Mechanical Technology, Busan National University, Korea. A weldment is locally heated by most welding processes, therefore, the temperature distribution in the weldment is not uniform, and metallurgical changes take place as welding progresses along the weld joint. Therefore, the welding residual stress is sometimes called restraint stress (Refs. 4, 5). These stresses can give rise to distortion and under certain circumstances even to premature failure. Hydrogen-assisted cracking is often detected at a notch in a weld made under restraint. Thus, residual stresses play an important role as far as the quality and reliability of a welded construction are concerned (Refs. 6, 7). One type of cold crack, referred to as a transverse crack, is caused by a complex interaction of the diffusible hydrogen supply, susceptible microstructure, and tensile residual stress. Previous papers on crack occurrence location, hardness, diffusible hydrogen contents, and microstructure, in accordance with welding conditions, were published in the Welding Journal and Journal of Japan Welding Society (Refs. 1-3). Hardness in the cracked area (deposited weld metal) was HV, and the FCAW and SAW electrodes had diffusible hydrogen contents of approximately 3-7 ml per 100 g of deposited weld metal by the glycerin method. The weld metal impact test showed KEY WORDS Residual Stresses Transverse Weld Cracks Preheat Interpass Temperatures Flux Cored Arc Welding (FCAW) Submerged Arc Welding (SAW) higher absorbed energy for the weld condition with preheating and interpass temperatures at C, compared to the specimen welded with preheating and interpass temperatures below 30 C. Transverse weld cracks were detected in the specimen welded with preheating and interpass temperatures below 30 C with the FCAW process. Cracks were detected mm from the weld face, between layers 5-8, while in the specimen welded with a preheat of 70 C, interpass temperature below 30 C, and using the SAW process, cracks occurred at mm from the weld face (Refs. 1-3). The transverse crack, a type of cold crack, occurs perpendicular to the axis of the weld interface. Therefore, longitudinal residual stresses are more important in transverse cracks. Until now, few investigations measuring residual stresses in the actual structure have been undertaken. In this study, specimens were fabricated and welded under conditions similar to actual construction conditions, then longitudinal residual stresses were measured for different welding conditions using the SAW and FCAW processes. Experimental Procedure Test Weldments: SAW Panel The test panel was prepared with a double-v groove and welded on two sides using a two-pole submerged arc process. The panel was EH32 TMCP (thermomechanical controlled process), high-strength hull steel (Table 1), to provide test conditions similar to actual construction conditions. To magnify fabrication-related weld residual stresses, the test panel was restrained by a jig, as shown in Fig. 1. The size of the test panel was 10 m (32.8 ft) long x 3.6 m (11.8 ft) wide x 50 mm (2 WELDING JOURNAL P.,PJ*I~"]

2 WELDING RESEARCH 3m 0.5m 3m 0.5m 3m i i i! cor~drno~ l i i CO,DmON, i icor~drnon m : : : = Fig Schematic diagram of weld panel for the SA W process. Fig Schematic diagram of the weld deposit metal for the SA W process. Table 1 -- Chemical Composition of Base/Weld Metal for the SAW Process (%) C Si Mn P S EH32 TMCP max. max. max. Base Metal Weld Metal A Weld Metal B Ni Mo V Ti T.S. Y.S. EL (N/mm2) (N/mm 2) (%) max. max. max. max. min. min A: preheating 70 C, interpass temp. below 30 C (10 mm from weld face of side 1). B: preheating 70 C, interpass temp C (10 mm from weld face of side I1). Table 2 -- Welding Parameters for SAW Process Pass No. Current (A) Voltage (V) Lead Trail Lead Trail (DCEP) (AC) Welding Heat Input (kj/cm) Speed Lead Trail (cm/min) Total Side I Side II Table 3 -- Preheating and Interpass Temperature for the SAW Process Preheating Interpass Temperature Condition Temperature Side I Side II Condition I 70 C C C Condition II 70 C C below 30 C Condition III 70 C below 30 C below 30 C in.) thick, as shown in Fig. 1. The panels were welded using AWS A5.17/F7AZ- EH14 electrode/flux combination with the SAW process using a tandem arc (4.8-mmdiameter electrodes with an extension of mm). The sections were welded under the following conditions: 1)A was welded with 70 C preheat (158 F) and interpass tem- peratures of C ( F); 2) B was welded with 70 C preheat and an interpass temperature below 30 C (86 F). The panel was welded in three parts (welding was interrupted at a 0.5-m width between welding conditions) with different interpass temperatures, as shown in Fig. 2. Welding parameters are shown in Tables 2 and 3. FCAW Panel The size of the test panel was 2 m (6.6 ft) long x 1.8 m (5.9 ft) wide x 50 mm (2 in.) thick. These test conditions were similar to actual construction conditions -- Fig. 3. To magnify fabrication-related weld residual stresses, the welding jig and test panel were fillet-welded together. Two sets of test panels were made the same size and morphology, as shown in Fig. 3. The specimen sections were welded in layers, as shown in Fig. 4. To compare the residual stresses and the places of transverse crack occurrence, the sections were welded under the following conditions: 1) One was welded below 30 C for preheating and interpass temperatures; 2) the other was welded with preheating and ~'~.[.'!$.-'! AUGUST 2003

3 , W E L D I N G R E S E A R C H "... :., A I 300 ~ 300 B 1,400 unit : mm D c [ WELDING DIRECTION D Fig Schematic diagram of weld panel for the FCA W process. B t C' A weld metal _u_nit.- mm \~/- 3o" ----.~/ // /// / 41 (A) ~X "1 Iroot gap: 10 (A - A') (B - B') /(A) B // ///////////// == IJ (c - c') section A- A' : 1/3-specimen thickness weld deposit metal section B- B' : 2/3-specimen thickness weld deposit metal section C-C' : full thickness weld deposit metal Fig The position of attached Rosette gauge for residual stress measurement of the cutting method. A -- FCA W process; B -- SA W process. Fig Schematic diagram of weld deposit metal for the FCA W process. A- A ~ -- ½-thickness of deposited weld metal; B-B ~ -- "/,-thickness of deposited weld metal; C-C I --full thickness of weld metal deposit. Table 4 -- Welding Parameters for the FCAW Process Identification Welding Pass Current Voltage Speed Heat Input Condition (A) (V) (cm/min) (kj/cm) A preheating/interpass temperature below 30 C B preheating/interpass temperature 100 ~ 120 C interpass temperatures of C ( F). The preheating temperature of 100 C was obtained with the Yurioka method (Ref. 8) (Table 4, 50-mm-thick steel plate, Ce. 0.34). The test specimens were welded at ] C in consideration of ambient temperatures. The panel was welded with AWS A5.29 E81T1-K2 electrodes, using the flux cored arc welding process (1.2 mm diameter, 20 L/min flow rate, 100% CO 2 gas, semiautomatic, electrode extension mm). Welding parameters are shown in Table 4. Chemical Composition/Strength A spectroanalyzer (Baird Spectrovac- 2000, USA) was used to determine the chemical composition of the base and weld metal. Mean values of the three specimens were then recorded in Tables 1 and 5, respectively. Strength was measured using a universal testing machine (Shimadzu UH- F100A, Japan). Tensile test specimens were made from all deposited metal in a direction parallel to the welding direction. The specimens were the round-bar type, taken 10 mm from the weld face, and recorded in Tables 1 and 5, respectively. Other test results such as hardness, microstructure, residual stresses, absorbed energy, diffusible hydrogen contents, and crack position were published in previous papers (Refs. 1-3). WELDING JOURNAL P.,l,.,hlS,"!

4 I 1 Fig. 8-- The transverse crack position according to changing welding conditions with the FCA W process. A ram weld joint; B mm weld joint. ;~,-~ i~. +,-~ll ~ ~-~-",,t.'~k,d~. Fig Macrostructure of weldments. A -- SA W process; B -- FCA W process. < Fig Optical micrographs of the transverse crack area taken from Fig. 9,4. 9+mm3- Fig. 7-- The transverse crack position according to changing welding conditions with the SAW process. A -- Preheat 70 C, interpass temp. 100~120 C both side I and side 2; B --preheat 70 C, interpass temp C (side 1), below 30 C (side 2); C -- preheat 70 C, interpass temp. below 30 C both side I and side 2. "~'~... I;... III'Hilll ' ~ i i' ' [ ":!II "li:ri if ~i i i 11tlt1+++ II+,l,lllll,++++L~+,+++++l]! ~+lil~t,i+~++~i ' t '! + 70 ao "1,,o Fig Morphology of transverse cracks after magnetic particle inspection for FCA W process. A mm depth from the weld face; B -- longitudinal section perpendicular to the plane of theplate. Distinction of Crack Position To check the position and length of the transverse cracks according to changing layer and preheating and interpass temperatures, the specimens were inspected by ultrasonic testing. The face of the weld bead was then cut at 0.5-mm-depth intervals using a milling machine and checked for accurate position and length of the transverse cracks using magnetic particle inspection after each machining step. Residual Stresses The residual stresses were measured using the Rosette gauge, hole-drilling method, per ASTM E (Ref. 9). The surface residual stresses of FCAW along the weld metal centerline (o x direction) were measured in the as-welded condition after the specimen cooled completely. To measure the longitudinal residual stresses as a function of depth in the joint, the specimens were machined to expose the longitudinal centerline, as shown in Fig. 5. The specimens were taken from the center of the test panel. Longitudinal residual stresses were measured for both the SAW and FCAW processes. In the specimen welded with SAW, the Rosette gauges were attached 3, 8, 15, 20, 25, 30, 35, 42, and 47 mm from the weld face. The specimens welded with the FCAW process had the Rosette gauges attached 3, 10, 20, 30, and 45 mm from the weld face. Results and Discussion Macrostructure Figure 6A and B shows the macrostructure of SAW and FCAW, respectively. The Fig. 6A panel was welded with preheating and interpass temperatures below 30 C, and 6B panels were welded with preheating at 70 C and interpass below 30 C. Position and Morphology of Crack Figure 7 shows the positions of transverse weld cracks for the SAW process. Transverse cracks were detected in the specimen welded with a preheat of 70 C and an interpass temperature below 30 C, as shown in Fig. 7. Cracks were not detected for the specimen welded with 70 C preheating and interpass temperatures of C. The cracks were detected mm from the weld face. P~.I:I$."I AUGUST 2003

5 WELDING RESEARCH 70 I 3O ~ "O-- preheating/interpass temp. below 30*(: ~ O'- preheating]interpass temp "C 0 ] [ 1 ] ] ] ] A B A B C D E F G Fig Surface residual stress of longitudinal direction in deposited metal with FCA W process. A --position of attached Rosette gauge; B -- distributions of surface residual stresses. Table 5 -- Chemical Composition of Base/Weld Metal for the FCAW Process (%) C Si Mn P S EH32 TMCP max. max. max. Base Metal Weld Metal A Weld Metal B Ni Mo V Ti T.S. Y.S. EL (N/mm 2) (N/mm 2) (%) max. max. max. max. min. min A: preheating and interpass temperature below 30 C ( 10 mm from weld face). B: preheating and interpass temperature C (l0 mm from weld face). Figure 8 shows the positions of transverse weld cracks for the FCAW process. Transverse cracks were detected in the specimen welded with preheating and interpass temperatures below 30 C, but cracks were not detected for the specimen welded with preheating and interpass temperatures of C. The cracks were detected at mm from the weld face. Figure 9 shows the morphology of transverse cracks for FCAW after magnetic particle inspection. Figure 9A shows the morphology of a crack at a 9.5 mm depth from the weld face. The cracks oriented perpendicularly to the welding axis. Figure 9B shows a longitudinal section perpendicular to the plane of the plates. The cracks were observed 45 deg to the longitudinal section, perpendicular to the plane of the plates. These cracks are called chevron cracks, transverse 45-deg cracking, or staircase cracking. Chevron cracking is the most used. The cracks are characterized by their orientation, which is approximately transverse to the welding direction and at 45 deg to the plane of the plate in a butt joint (Refs. 10, 11). Figure 10A and B shows an optical micrograph of the transverse crack area. The formation of these cracks did not follow the grain boundary ferrite, rather, they propagated across the grains. From fracture morphology, it is noted that transverse cracks occur in high stresses. Residual Stresses Figure 11 shows the longitudinal surface residual stresses for FCAW. The residual stresses were measured at the surface of the deposited metal in a longitudinal direction to the weld interface. In all measured points, the residual stress values for specimens welded with preheating and interpass temperatures below 30 C were higher than those welded with preheating and interpass temperatures of C. Figure 12 shows the residual stresses of longitudinal stresses as a function of depth in the joint for SAW The residual stresses were measured in the longitudinal direction of the deposited metal. For most of the measured points, the residual stress values for a specimen welded with 70 C preheating and interpass temperatures below 30 C were higher than for specimens preheated at 70 C and with interpass temperatures of C. For the same method, residual stresses measured in the longitudinal direction of the deposited metal for FCAW are shown in Fig. 13. For most of measured points, the residual stress values for a specimen welded with preheating and interpass temperatures below 30 C were higher than the specimens with preheating and interpass temperatures of C. Slightly higher residual stresses were measured in welds with lower preheat and interpass temperatures, but the deviation of residual stresses measured for as-welded conditions may be higher than that of residual stresses measured in a small machined test piece. The residual stress values for a specimen measured at the weld surface, in the as-welded condition, were higher than longitudinal residual stresses that were measured from a small test piece at the same position. The residual stress values were about five times higher as shown in Figs. 11 and 13. This was because the residual stress was relieved during the machining process, before residual stress measurement. The tendency of residual stress agreed with other research (Refs. 12, 13). In multipass welds, residual stress is distributed nonuniformly. Gunnert (Ref. 12) has shown the directions of residual stress distribution in lowcarbon steel weld metal in a 1-in. (25 mm)- thick butt joint. Welding was sequenced alternately on both sides to minimize angular distortion. High longitudinal tensile residual stresses were found in the areas near the surface of the weld. Transverse cracks were detected in area of the maximum residual stress for both the SAW and FCAW processes. The residual stresses and hydrogen accumulation may be at a maximum in those loca- WELDING JOURNAL i,.~.,[4n~..i

6 preheat 7012, interpass temp (condition I ) (D preheat 7012, interpass temp. below 3012(condition l]i) preheat/ interpass temperature preheat] interpass temperature below 30"12 Top surface Side II E g ( Side l I ' I ' I ' I Residual stress(kgjmm 2) Root o.oo ~ I ~ I ' I ' 1 ' I Residual stress(kg/mm ~) Fig Distributions of longitudinal residual stress as a function of depth in the joint for SA W process. Fig Distributions of longitudinal residual stress as a function of depth in the joint for the FCA W process. tions (Ref. 14). It is believed they directly affected transverse crack occurrence. Conclusions The relationship for residual stresses, longitudinal stresses, and transverse weld cracks was studied for EH32 TMCP 50- mm-thick plate welded with the SAW and FCAW processes. The results of this study can be summarized as follows: 1) Transverse weld cracks were detected in the specimen welded with preheating and interpass temperatures below 30 C with the FCAW process. The cracks were detected mm from the weld face. In the specimen welded with 70 C preheating and an interpass temperature below 30 C using the SAW process, cracks were detected mm from the weld face. 2) The formation of transverse weld cracks did not follow the grain boundary ferrite, rather, they propagated across the grains. From fracture morphology, it is noted that transverse cracks occur in high stress areas. 3) The residual stress values for a specimen measured at the weld surface, in the as-welded condition, was higher than that of longitudinal residual stresses measured from a small test piece due to the relief of residual stresses by the cutting and machining processes. 4) The residual stress values for the specimen welded with an interpass temperature below 30 C was higher than the specimen welded at interpass temperatures of C. Transverse weld cracks were detected in the area of the maximum residual stresses for both the SAW and FCAW processes. References 1. Lee, H. W., Kang, S. W., and Um, D. S A study on transverse weld cracks in thick steel plate with the FCAW process. Welding Journal 77(12): 503-s to 510-s. 2. Lee, H. W, Kang, S. W, and Park, J. U Fatigue strength depending on position of transverse cracks in FCAW process. Welding Journal 80(6): 137-s to 141-s. 3. Lee, H. W., and Kang, S. W A study on transverse weld cracks in 50-mm-thick steel plate with the SAW process. Journal of Japan Welding Society 15(4): Kou, S Welding Metallurgy. New York, N.Y: John Wiley and Sons, pp Brand, P. C., De Keijser, Th. H., and Den Ouden, G Welding Journal 72(3): 93-s to 100-s. 6. Yurioka, N., and Suzuki, H Hydrogen assisted cracking in C-Mn and low alloy steel weldments. International Materials Reviews 35(4): Hart, E H. M Resistance to hydrogen cracking in steel weld metals. Welding Jourhal 65(1): 14-s to 22-s. 8. Yurioka, N A chart method to determine necessary preheat temperature in steel welding. Journal of Japan Welding Society, pp ASTM Test Method E Standard Test Method for Determining Residual Stresses by the Hole-Drilling Strain-Gauge Method. 10. Mota, J. M. E, and Apps, R. L Chevron cracking -- a new form of hydrogen cracking in steel weld metals. Welding Journal 61(7): 222-s to 228-s. i1. Allen, D. J., Chew, B., and Harris, P The formation of chevron cracks in submerged arc weld metal. Welding Journal 61(7): 212-s to 221-s. 12. Welding Handbook, 8th ed., Vol. 1. Welding technology. Miami, Fla.:American Welding Society, pp , Shim, Y., Feng, Z., Lee, S., Ki, D., and Jaeger, J. C Determination of residual stresses in thick-section weldments. Welding Journal 71(9): 305-s to 312-s 14. Takahashi, E Relations between occurrence of the transverse cracks. Journal of Japan Welding Society, pp REPRINTS REPRINTS To order custom reprints of articles in WeMing Journal, contact Denis Mulligan at (800) FAX: (717) or via at inf com REPRINTS REPRINTS i,.g[=l~-t AUGUST 2003